CN113681148B - Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method - Google Patents
Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method Download PDFInfo
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- CN113681148B CN113681148B CN202110992426.XA CN202110992426A CN113681148B CN 113681148 B CN113681148 B CN 113681148B CN 202110992426 A CN202110992426 A CN 202110992426A CN 113681148 B CN113681148 B CN 113681148B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
- B23K20/127—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding friction stir welding involving a mechanical connection
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
- B23K20/1245—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding characterised by the apparatus
- B23K20/1255—Tools therefor, e.g. characterised by the shape of the probe
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/584—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B37/00—Joining burned ceramic articles with other burned ceramic articles or other articles by heating
- C04B37/02—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles
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- Chemical & Material Sciences (AREA)
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- Structural Engineering (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
- Ceramic Products (AREA)
Abstract
The invention relates to a tool component for friction stir welding, which is characterized in that: in a tool member for friction stir welding composed of a ceramic member in which a shoulder portion and a pin portion are integrated, the root portion of the pin portion and the end portion of the shoulder portion have curved surfaces, and R1/D is 0.02 to 0.20 when the radius of curvature of the end portion of the shoulder portion is R1 (mm) and the outer diameter of the shoulder portion is D (mm). The ceramic member is preferably made of a silicon nitride sintered body having a vickers hardness of 1400HV1 or more. According to the above configuration, a tool member for friction stir welding having excellent durability can be provided.
Description
The present application is a divisional application of patent application having a filing date of 2017, 8, 4, and a chinese application number of 201780048238.3 and having the name of "tool member for friction stir welding and friction stir welding apparatus using the same".
Technical Field
Embodiments relate to a tool member for friction stir welding, a friction stir welding apparatus using the same, and a friction stir welding method.
Background
Friction stir welding (FSW: friction Stir Welding) is a welding method in which a welding tool member called a probe (probe) is pressed against the member while rotating the member at a high speed, and a plurality of members are integrated by friction heat. The members (base material) are softened by frictional heat, and plastic flow is generated around the welded portion by the torque of the stirring pin, so that the members (base material and corresponding material) can be integrated. Friction stir welding is therefore said to be one type of solid phase welding.
Since friction stir welding is solid phase welding, the amount of heat input to the welded portion is small, and thus the degree of softening and strain of the welded object is small. In addition, since no solder is used, cost reduction can be expected. The welding tool member used in friction stir welding requires abrasion resistance that can withstand high-speed rotation and heat resistance that can withstand frictional heat. As a conventional bonding tool member, a member using a silicon nitride sintered body is disclosed in japanese patent application laid-open No. 2011-98842 (patent document 1). The silicon nitride sintered body of patent document 1 is a sintered body containing cBN (cubic boron nitride), siC (silicon carbide), and TiN (titanium nitride) in a large amount of up to 20 vol%.
Although the welding tool member made of the silicon nitride sintered body of patent document 1 can exhibit a certain improvement in wear resistance, further improvement is required. It has been found that, in a sintered body in which cBN (cubic boron nitride), siC (silicon carbide) and TiN (titanium nitride) are added in a large amount of up to 20vol%, as in patent document 1, a dense sintered body cannot be obtained because of the difficulty in sintering, and the abrasion resistance of the silicon nitride sintered body is insufficient.
On the other hand, in the invention described in international publication No. WO2016/047376 (patent document 2), a friction stir welding tool member made of a silicon nitride sintered body was developed in which the amount of a sintering aid was set to 15 mass% or less. By setting the sintering aid to a prescribed combination, a reduction in the amount of sintering aid is achieved.
Prior art literature
Patent literature
Patent document 1: japanese patent laid-open publication No. 2011-98842
Patent document 2: international publication No. WO2016/047376
Disclosure of Invention
Problems to be solved by the invention
The friction stir welding tool member according to the embodiment is completed to solve such a problem.
Means for solving the problems
The embodiment relates to a friction stir welding tool component, which is characterized in that: in a friction stir welding tool comprising a ceramic member in which a shoulder portion and a pin portion are integrated, the root portion of the pin portion and the end portion of the shoulder portion have curved surfaces, and R1/D is 0.02 to 0.20 when the radius of curvature of the end portion of the shoulder portion is R1 (mm) and the outer diameter of the shoulder portion is D (mm).
Drawings
Fig. 1 is a half cross-sectional view showing an example of the structure of a friction stir welding tool member according to an embodiment.
Fig. 2 is a cross-sectional view showing an example of the inclination angle of the inclined surface of the tool member.
Detailed Description
The embodiment relates to a friction stir welding tool component, which is characterized in that: in a friction stir welding tool comprising a ceramic member in which a shoulder portion and a pin portion are integrated, the root portion of the pin portion and the end portion of the shoulder portion have curved surfaces, and R1/D is 0.02 to 0.20 when the radius of curvature of the end portion of the shoulder portion is R1 (mm) and the outer diameter of the shoulder portion is D (mm).
Fig. 1 is a half cross-sectional view showing an example of a friction stir welding tool member according to an embodiment. In the figure, symbol 1 denotes a friction stir welding tool member, 2 denotes a distal end portion of a pin portion, 3 denotes an end portion of a shoulder portion, 4 denotes a root portion of the pin portion, 5 denotes an inclined surface, W denotes an outer diameter of the pin portion, and D denotes an outer diameter of the shoulder portion.
The friction stir welding tool member 1 is composed of a ceramic member in which a shoulder portion and a pin portion are integrated. The term "integrated" means a state in which the shoulder portion and the pin portion are formed of one ceramic sintered body. For example, the step portion and the stirring pin portion are welded together by a solder. Also, the structure in which the shoulder portion and the stirring pin portion are fitted together is excluded.
The shoulder portion and the stirring pin portion are designed to be an integrated structure of one ceramic sintered body, so that the strength of the tool member can be improved.
The root portion of the pin portion and the end portion of the shoulder portion have a curved surface shape. The stirring pin part is a convex part at the top end of the tool component. Friction stir welding is performed by pushing the convex portion (pin portion) against the material to be welded. The root of the convex portion becomes the root. By setting the root portion to a curved shape, the strength of the root portion can be improved. In the case of rotating at a high speed like a tool member, if the root is at a right angle, the stirring pin portion is likely to break. By imparting a curved shape to the root, concentration of stress can be prevented.
In addition, the end of the shoulder portion is also characterized by having a curved shape. If the pin portion is pushed onto the material to be welded during friction stir welding, the shoulder portion contacts the material to be welded. If the end of the shoulder portion is square, the contact between the end and the material to be welded becomes a line contact state. In the case of the wire contact, the end portion of the shoulder portion is excessively stressed, and thus the end portion is easily broken. In contrast, by setting the end portion of the shoulder portion to have a curved shape, the end portion of the shoulder portion and the material to be welded can be brought into surface contact. Thus, the occurrence of breakage of the shoulder portion can be effectively suppressed.
When the radius of curvature of the end portion of the shoulder portion is R1 (mm) and the outer diameter of the shoulder portion is D (mm), R1/D is set in the range of 0.02 to 0.20.
The radius of curvature R1 of the end portion of the shoulder portion is obtained by cross-sectional observation or image analysis (image analysis of the tool member (three-dimensional) state) of the tool member. The outer diameter D of the shoulder portion is set to the outer diameter of the tool member (ceramic member). When the stirring pin portion side is seen from the front, the longest diameter of the shoulder portion is set as the outer diameter D of the tool member.
R1/D is 0.02 to 0.20, and the radius of curvature R1 is set to be in the range of 2 to 20% relative to the outer diameter D (mm). By the presence of the shoulder portion, the strength as a tool member is improved. In addition, by bringing the shoulder portion into contact with the material to be welded, the stirring force is improved.
In the shape where the shoulder portion is not present, the stirring pin portion is formed in an elongated shape. In the elongated shape, the tool member is easily broken. The strength of the tool component may be increased if a shoulder portion is present. On the other hand, if the end of the shoulder portion is square, the shoulder portion is liable to be broken.
By setting the R1/D to 0.02 to 0.20, the strength of the entire tool member can be improved and the strength of the shoulder end portion can be improved. When R1/D is less than 0.02, the curvature radius R1 of the end portion of the shoulder portion is too small, and the effect of setting the curved shape is insufficient. In addition, when R1/D exceeds 0.20, the radius of curvature R1 increases. If the radius of curvature R1 is too large, the shoulder portion becomes elongated, and the strength of the tool member decreases. Accordingly, R1/D is preferably 0.02 to 0.20, and more preferably 0.05 to 0.15.
The radius of curvature R1 of the end portion of the shoulder portion is preferably 0.5mm or more. When the radius of curvature R1 is less than 0.5mm, it is difficult to control R1/D in the range of 0.02 to 0.20. In particular, in order to design such a shape in the ceramic member, it is necessary to thin the outer diameter D of the shoulder portion, and thus processing is difficult. The upper limit of the radius of curvature R1 is not particularly limited, but the radius of curvature R1 is preferably 4mm or less. If the radius of curvature R1 is large exceeding 4mm, the shoulder portion becomes a shoulder-sliding shape. By the presence of the shoulder portion, the penetration depth of the pin portion into the material to be welded can be stabilized in friction stir welding. If the shoulder portion is shaped like a shoulder, it is difficult to stabilize the depth of the pin portion into the material to be welded. Therefore, the radius of curvature R1 of the end portion of the shoulder portion is preferably 0.5mm to 4mm, and more preferably 1.2mm to 2.3mm.
When the radius of curvature of the root of the pin portion is set to R2 (mm), R2 is preferably 0.1mm or more. If the radius of curvature R2 is less than 0.1mm, the root of the pin portion becomes nearly rectangular, and the strength of the structure of the pin portion is reduced. The shape of the root may be a gentle curved surface shape such as a shape of a field under the foot of a Fuji mountain. On the other hand, by setting the radius of curvature R2 to 0.1mm or more, the strength of the structure of the root portion can be improved. In addition, the stirring force generated by the stirring pin part is improved.
Further, it is preferable that an inclined surface is provided from the end of the shoulder portion to the root of the stirring pin portion. As shown in fig. 2, the inclined surface is formed to descend from the end of the shoulder portion toward the center of the stirring pin. That is, the inclined surface is disposed so that a concave portion is formed around the tip end portion 2 of the stirring pin. Therefore, the horizontal direction of the stirring pin forms a predetermined inclination angle θ with the inclined surface.
The inclination angle θ of the inclined surface is preferably more than 0 ° and 10 ° or less. The inclination angle θ of the inclined surface is more preferably 3 to 8 °.
Fig. 2 shows an example of the configuration of the inclined surface 5 extending from the end 3 of the shoulder portion to the root 4 of the pin portion. The inclination angle θ of the inclined surface indicates an angle between a horizontal line (broken line in fig. 2) and the inclined surface 5 when the horizontal line is drawn from the lowermost portion of the root portion 4 of the pin portion.
By providing the inclined surface, stress concentration at the root portion 4 of the pin portion in friction stir welding can be prevented. In addition, since the end portion 3 of the shoulder portion is formed in a curved shape, the shoulder portion can be prevented from coming into line contact with the material to be welded. By combining and forming the inclined surfaces 5, the durability of the tool member 1 can be improved.
The inclination angle θ of the inclined surface is preferably more than 0 ° and 10 ° or less, and more preferably 3 to 8 °. If the inclination angle θ is large exceeding 10 °, the end portion 3 of the shoulder portion easily becomes in line contact with the material to be welded. In addition, if the inclination angle θ is 0 ° (horizontal), stress is easily applied to the root of the stirring pin portion.
The inclination angle θ of the inclined surface is preferably less than 0 ° and equal to or greater than-10 °, and more preferably from-3 ° to-8 °. If the inclination angle θ of the inclined surface is smaller than-10 °, stress is easily applied to the root of the stirring pin portion. By setting the inclination angle θ of the inclined surface to be less than 0 ° and equal to or more than-10 °, the material to be welded can be easily stirred by the stirring pin portion. Further, since the root portion of the stirring pin portion is formed in a curved shape, durability is not reduced even if the inclination angle is inclined in the opposite direction.
The outer diameter W of the pin portion is preferably not more than 0.7D (mm) relative to the outer diameter D of the shoulder portion. If the outer diameter W (mm) of the pin portion is close to the outer diameter D (mm) of the shoulder portion, the effect of providing the shoulder portion is small.
The tip end portion 2 of the stirring pin portion is preferably curved. If the tip end portion 2 of the pin portion is spherical, the member to be welded is likely to enter during friction stir welding. If the tip end 2 is a flat surface, the tip end 2 of the stirring pin is square. If square, cracks are liable to occur, and the life is reduced. Therefore, the distal end portion of the stirring pin portion is preferably curved.
The surface roughness Ra of the tip 2 of the stirring pin is preferably 10 μm or less, more preferably 5 μm or less. The surface roughness Ra of the end portion 3 of the shoulder portion is also preferably 10 μm or less, and more preferably 5 μm or less. If the surface roughness of the tip end portion 2 of the pin portion and the end portion 3 of the shoulder portion is reduced, it is possible to prevent the tool member from being damaged by contact with the material to be welded in friction stir welding.
The surface roughness Ra is preferably 3 μm or less, and more preferably 2.5 μm or less. The lower limit of the surface roughness Ra is not particularly limited, but is preferably 0.01 μm or more. When Ra is small and less than 0.01 μm, the adhesion between the tip end portion 2 of the stirring pin and the member to be welded is improved, while the stirring force of the tip end portion 2 of the stirring pin is reduced.
Here, the stirring force of the tip end portion 2 of the stirring pin portion is a force that causes plastic deformation (plastic flow) of the welded member. If the stirring force is insufficient, the welding force between the welded members decreases. In addition, plastic deformation of the welded member takes time, and it is also considered that the welding time is prolonged. Therefore, the surface roughness Ra of the tip 2 of the stirring pin is preferably 0.01 to 5. Mu.m, more preferably 0.05 to 2.5. Mu.m.
The ceramic member is preferably made of a silicon nitride sintered body having a vickers hardness of 1400HV1 or more. The Vickers hardness HV1 was set to a value measured under a load of 1kg in accordance with JIS-R1610.
The vickers hardness HV1 is preferably 1400 or more, and more preferably 1500 or more. The upper limit of the vickers hardness is not particularly limited, but is preferably 1900HV1 or less. If the Vickers hardness is high exceeding 1900HV1, it is difficult to process into a curved shape. In view of workability, the silicon nitride sintered body preferably has a vickers hardness HV1 of 1400 to 1900, more preferably 1500 to 1700.
The silicon nitride sintered body preferably contains 15 mass% or less of an additive component other than silicon nitride, and the additive component contains 3 or more elements selected from Y, lanthanoid, and Al, mg, si, ti, hf, mo, C.
That is, the silicon nitride sintered compact contains 15 mass% or less of the additive component. The additive component means a component other than silicon nitride. The additive component other than silicon nitride in the silicon nitride sintered body means a sintering aid component. The sintering aid component constitutes the grain boundary phase. If the content of the additive component is excessive and exceeds 15 mass%, the grain boundary phase is excessive. The silicon nitride sintered body has a structure in which elongated β -silicon nitride crystal particles are entangled with each other. If the sintering aid component is increased, it is not preferable to form a part of the structure where the silicon nitride crystal particles do not become entangled with each other in a complicated manner.
The amount of the additive component is preferably 3 to 12.5 mass%. The content of the additive component is more preferably 5 to 12.5 mass%. If the additive content is less than 3 mass%, the grain boundary phase transition becomes too small, and the density of the silicon nitride sintered body may be lowered. If the additive component is 3 mass% or more, the relative density of the sintered body is easily 95% or more. Further, by setting the additive component to 5 mass% or more, the relative density of the sintered body can be easily made 98% or more.
The additive component preferably contains 3 or more elements selected from Y, lanthanoid, and Al, mg, si, ti, hf, mo, C. The form of the presence of Y (yttrium), lanthanoid, al (aluminum), mg (magnesium), si (silicon), ti (titanium), hf (hafnium), mo (molybdenum), and C (carbon) as the additive components is not limited as long as the components are contained. Examples thereof include forms such as oxides (including composite oxides), nitrides (including composite nitrides), oxynitrides (including composite oxynitrides), and carbides (including composite carbides). The lanthanoid element is preferably 1 kind selected from Yb (ytterbium), er (erbium), lu (lutetium), and Ce (cerium).
As described later, when added as a sintering aid in the production process, oxides (including composite oxides), nitrides (including composite nitrides), and carbides (composite carbides) are preferable. In the case of element Y, yttrium oxide (Y 2 O 3 ). The lanthanoid element is preferably selected from ytterbium oxide (Yb 2 O 3 ) Erbium oxide (Er) 2 O 3 ) Ruthenium oxide (Lu) 2 O 3 ) Cerium oxide (CeO) 2 ) 1 of them.
In the case of Al element, alumina (Al 2 O 3 ) Aluminum nitride (AlN), mgO.Al 2 O 3 Spinel. In the case of Mg element, magnesium oxide (MgO) and MgO.Al are preferable 2 O 3 Spinel. In the case of Si element, silicon oxide (SiO 2 ) Silicon carbide (SiC).
In the case of Ti element, titanium oxide (TiO 2 ) Titanium nitride (TiN). In addition, in the case of the Hf element, hafnium oxide (HfO 2 ). In the case of Mo element, molybdenum oxide (MoO 2 ) Molybdenum carbide (Mo) 2 C) A. The invention relates to a method for producing a fibre-reinforced plastic composite The C element is preferably added as silicon carbide (SiC), titanium carbide (TiC), or titanium carbonitride (TiCN). By adding 2 or more of these additive components in combination, a grain boundary phase having 3 or more elements selected from Y, lanthanoid, al, mg, si, ti, hf, mo, C can be constituted. The additive component preferably contains 4 or more elements selected from Y, lanthanoid, and Al, mg, si, ti, hf, mo, C.
The following combinations are preferred as the combinations of sintering aids to be added in the production process.
First, as a first combination, 0.1 to 1.7 mass% MgO and 0.1 to 4.3 mass% Al are added 2 O 3 0.1 to 10 mass% of SiC and 0.1 to 2 mass% of SiO 2 . Thus, these 4 kinds of Mg, al, si, C are contained as additive components. In addition, after adding MgO and Al 2 O 3 In the case of (C), mgO-Al may be used 2 O 3 The spinel is added in an amount of 0.2 to 6 mass%.
In the first combination, 0.1 to 2 mass% of TiO may be added 2 . By adding TiO in the first combination 2 Then, 5 of Mg, al, si, C, ti are contained as additive components.
Further, as the second combination, 0.2 to 3 mass% of Y is added 2 O 3 0.5 to 5 mass% of MgO/Al 2 O 3 Spinel, 2 to 6 mass% of AlN, 0.5 to 3 mass% of HfO 2 0.1 to 3 mass% of Mo 2 C. The second combination adds Y, mg, al, hf, mo, C these 6 kinds as additive components.
In addition, oxides of lanthanoid elements can also be used instead of Y 2 O 3 . In this case, addThe 6 lanthanoids are added, mg, al, hf, mo, C.
In addition, as a third combination, 2 to 7 mass% of Y is added 2 O 3 3 to 7 mass% of AlN and 0.5 to 4 mass% of HfO 2 . Thus, the additive components were set to 3 kinds of Y, al, and Hf.
In addition, oxides of lanthanoid elements can also be used instead of Y 2 O 3 . In this case, 3 kinds of lanthanoid elements, al, hf are set.
In the first to third combinations, the total upper limit of the content of the sintering aid components is set to 15 mass% or less.
In the first to third combinations, Y is not added 2 O 3 And Al 2 O 3 Is a combination of (a) and (b). First combination unused Y 2 O 3 . In addition, the second combination is MgO.Al 2 O 3 Spinel is added in the form of a spinel. In addition, the third combination does not use Al 2 O 3 。Y 2 O 3 And Al 2 O 3 If the combination of (a) is sintered, YAG (Al) 5 Y 3 O 12 )、YAM(Al 2 Y 4 O 9 )、YAL(AlYO 3 ) Yttrium aluminum oxide. These yttrium aluminum oxides have poor heat resistance. The same applies even if Y is replaced with a lanthanoid. The friction stir welding tool member has a friction surface in a high-temperature environment at 800 ℃ or higher. If the heat resistance is lowered, the durability of the bonding tool member is lowered.
The additive component also has an excellent effect as a sintering aid. Therefore, the aspect ratio of the β -type silicon nitride crystal particles can be increased by 60% or more by 2 or more. The ratio of the aspect ratio to 2 or more was determined by the following procedure. That is, an SEM observation was performed on an arbitrary cross section of the silicon nitride sintered body to take a magnified photograph (magnification: 3000 times or more). Next, the long diameter and the short diameter of the silicon nitride crystal particles photographed by the enlarged photograph were measured to determine the aspect ratio. The area ratio (%) of silicon nitride crystal particles having an aspect ratio of 2 or more per unit area of 50 μm×50 μm was determined.
In addition, in the friction stir welding apparatus, in order to shorten the welding time of the material to be welded and to improve the productivity, it is preferable that the welding tool member is rotated at a rotation speed of 300rpm or more and used under a press-in load of 9.8kN (1 ton) or more. In addition, under the action of friction heat, the friction surface is in a high-temperature environment with the temperature of more than 800 ℃. Therefore, the tool member requires heat resistance and wear resistance. Such a silicon nitride sintered body welding tool member requires a vickers hardness and a fracture toughness value.
The vickers hardness of the silicon nitride sintered body can be set to 1400HV1 or more by the additive component. The fracture toughness value of the silicon nitride sintered body is preferably 6.0 MPa.m 1/2 The above. Further, the Vickers hardness may be set to 1500HV1 or more, and the fracture toughness value may be set to 6.5 MPa.m 1/2 The above. The 3-point bending strength may be 900MPa or more, and further 1000MPa or more.
The welding tool member for friction stir welding, which is composed of the ceramic member described above, is excellent in heat resistance and wear resistance. Therefore, the steel sheet exhibits excellent durability even in a severe welding environment in which the rotational speed is 300rpm or more and the press-in load is 9.8kN (1 ton) or more. In the case of wire bonding, the moving speed may be set to 300 mm/min or more.
The rotation speed of the tool member is preferably in the range of 300rpm to 1000rpm as the condition of the friction stir welding step. At a rotation speed of less than 300rpm, the stirring force may be insufficient. If the stirring force exceeds 1000rpm, the stirring force is too strong, and the irregularities of the weld marks of the welded material are increased. If the irregularities of the weld mark are increased, the appearance is deteriorated. Therefore, the rotation speed is preferably 300 to 1000rpm, and more preferably 400 to 800 rpm.
The press-in load is preferably 9.8kN to 50kN. At less than 9.8kN, the stirring force is insufficient. In addition, if it exceeds 50kN, the life of the tool member may be reduced. Therefore, the press-in load is preferably in the range of 14kN to 35 kN.
The rotation speed and the press-in load can be applied to any case of spot welding and wire welding. In the case of wire bonding, the moving speed is preferably in the range of 300 mm/min to 1500 mm/min. At a movement speed below 300 mm/min, the speed is too slow to reduce mass productivity. On the other hand, if it is faster than 1500rpm, the stirring force is locally reduced, and the welding strength between the materials to be welded is reduced. Therefore, the moving speed is preferably 300 to 1500 mm/min, more preferably 400 to 1000 mm/min.
The bonding tool member according to the embodiment may be used under conditions of a rotational speed of less than 300rpm and a press-in load of less than 9.8 kN.
When the rotational speed of the tool member is set to a (rpm) and the torque is set to B (kg·m), B/a=0.001 to 0.025 is preferable. The torque is expressed as the product of force and distance. The unit of torque was kg·m. In addition, 1kg·m=9.8n·m. B/a=0.001 to 0.025 means that the torque is sufficiently large relative to the rotational speed. If the rotation speed is large, the stirring force increases. The predetermined torque can be maintained while the rotational speed is maintained. Even with such a use method, excellent durability can be exhibited. Further, if the ratio B/a=0.001 to 0.025, a defect-free welded portion can be formed.
The torque is calculated by using a servo motor for rotating the tool material of the friction stir welding device as a torque computer. Here, a servo motor (servo) is a motor used for controlling a position, a speed, and the like in a servo mechanism. An analog/digital conversion unit for capturing a voltage of about DC0V to DC10V from the monitor output of the servo amplifier to a sequencer. Then, the analog voltage captured by the internal operation of the sequencer is converted into a digital voltage. The torque is calculated by using a calculation formula suitable for the operation mode.
Even under the above conditions, the friction stir welding tool member of the embodiment exhibits excellent durability. In addition, the steel wire rod has excellent durability even in a severe welding environment in which the temperature of the tip end of the stirring pin is 800 ℃ or higher.
Therefore, the welding machine is suitable for welding operations in which the material to be welded is steel. Specific examples of the steel include iron alloys such as stainless steel, carbon steel, and high-strength steel. Steel can be used for various products such as automobiles, railways, machine tools, furniture and the like. Friction stir welding is a welding method that does not use a solder, and is therefore effective for weight reduction of products and the like.
Steel is a material having a thickness of 0.5mm or more, and further a material having a thickness of 1mm or more. Further, the friction stir welding is performed by overlapping 2 or more pieces of welding target material, and therefore the upper limit of the steel thickness is preferably 3mm or less. Therefore, the aforementioned severe welding conditions are required. The friction stir welding tool member according to the embodiment is excellent in durability and can be used even under the severe conditions described above.
In addition to the friction stir welding, the friction stir welding is a method of welding materials to be welded together by joining the materials to be welded together. In addition, the method may be a wire welding method or a spot welding method (spot welding method). Further, the method can be applied to a Friction Stir Process (FSP) using friction stir. In other words, in an embodiment, friction Stir Welding (FSW) includes a Friction Stir Process (FSP).
In the friction stir welding step, a backing material is used as needed. The backing material is preferably composed of a silicon nitride sintered body.
Next, a method for manufacturing a friction stir welding tool member according to an embodiment will be described. The method of manufacturing the friction stir welding tool member according to the embodiment is not particularly limited as long as the member has the above-described structure, but the following methods are exemplified as a method for efficiently obtaining the member.
First, a ceramic sintered body was produced. The ceramic sintered body is preferably a silicon nitride sintered body. The silicon nitride sintered body preferably contains 15 mass% or less of an additive component other than silicon nitride, and the additive component has 3 or more elements selected from Y, lanthanoid, al, mg, si, ti, hf, mo, C.
On the other hand, silicon nitride powder was prepared. The silicon nitride powder is preferably an α -type silicon nitride powder having an average particle diameter of 2 μm or less. By using such a silicon nitride powder, the α type is changed to the β type in the sintering step, and thus a structure in which β type silicon nitride crystal particles are entangled with each other can be realized. The impurity oxygen content in the silicon nitride powder is preferably 2 mass% or less.
Next, a sintering aid powder is prepared as an additive component. The sintering aid powder is set to have a combination of 3 or more elements selected from the group consisting of Y, lanthanoid, al, mg, si, ti, hf, mo, C. The form of addition is 1 or more selected from oxide powder (including composite oxide), nitride powder (including composite nitride), carbide powder (including composite carbide), and carbonitride (including composite carbonitride). The total amount is 15 mass% or less. The average particle diameter of the sintering aid powder is preferably 3 μm or less. Among the preferred combinations of the sintering aid powders, the aforementioned first to third combinations are suitable.
Next, the silicon nitride powder and the sintering aid powder are mixed, and then mixed by a ball mill, thereby preparing a raw material powder. Then, an organic binder is added to the raw material powder to perform a molding step. The molding step may use a mold having a target shape. Further, a molded body having a cylindrical shape or a quadrangular prism shape may be produced. In addition, as the molding step, mold molding, CIP (cold isostatic pressing), or the like may be used.
Next, the molded body obtained in the molding step is degreased. The degreasing step is preferably performed at a temperature of 400 to 800 ℃ in nitrogen. Further, the molded body may be processed to be close to the target shape.
Next, the degreased body obtained in the degreasing step is sintered. The sintering step is performed at a temperature set to 1600 ℃ or higher. The sintering step is preferably performed in an inert atmosphere or in vacuum. As the inert atmosphere, nitrogen atmosphere and argon atmosphere can be cited. The sintering step includes normal pressure sintering, and HIP (hot isostatic pressing). In addition, a plurality of sintering methods may be combined.
The obtained silicon nitride sintered body is finally processed into a desired shape. The machining is preferably grinding machining or electric discharge machining. For the curved shape of the root of the stirring pin portion, electric discharge machining is suitable. The polishing is preferably a polishing using diamond grindstone. Further, the polishing process using diamond grindstone is also suitable for adjusting the surface roughness of the distal end portion of the stirring pin portion and the end portion of the shoulder portion.
Example (example)
(examples 1to 9 and comparative examples 1to 3)
As the ceramic member, a raw material mixed powder to which the silicon nitride powder and the sintering aid powder shown in table 1 were added was prepared. The silicon nitride powder has an alpha-ratio of 95% or more and an average particle diameter of 1.2 μm. The sintering aid powder has an average particle diameter of 0.7 to 2.0. Mu.m.
TABLE 1
Next, the raw material mixed powders of the respective samples were mixed by a ball mill, and then 2 mass% of an organic binder was mixed. Then, the mold is formed. Next, each molded body was sintered under normal pressure in a nitrogen atmosphere at a temperature of 1800℃for 5 hours. Then, HIP sintering was performed at 1700 ℃ for 2 hours. Thus, silicon nitride sintered bodies of samples 1to 6 were produced.
The obtained silicon nitride sintered body was measured for vickers hardness, fracture toughness value, and 3-point bending strength. Vickers hardness HV1 was tested in accordance with JIS-R1610 under a load of 1 kg. The fracture toughness value was measured according to JIS-R-1607, and was obtained from the original formula based on the IF method. Further, the 3-point bending strength was measured in accordance with JIS-R1601. The results are shown in Table 2 below.
TABLE 2
Next, each sample was processed to produce a tool member. The tool member had an outer diameter D of the shoulder portion of 20mm and an outer diameter W of the stirring pin portion of 10mm. In each of examples and comparative examples 1 and 2, the tip end portion of the stirring pin portion was set to have a curved shape. As shown in table 3, the end of the shoulder portion and the root of the pin portion were curved (see fig. 1). In addition, electric discharge machining is used for machining the curved surface shape.
As comparative example 3, a sample was prepared using the silicon nitride sintered body of example 1, and the end of the shoulder portion and the root of the stirring pin portion were set to have a rectangular shape.
In the tool members of the examples and comparative examples, the surface roughness Ra of the end portion of the shoulder portion and the tip end portion of the stirring pin portion was uniform to 2 μm. The surface roughness is adjusted by polishing using diamond grindstone.
TABLE 3 Table 3
Next, the friction stir welding tools of each of the examples and comparative examples were set in a friction stir welding apparatus. As a material to be welded, 2 pieces of stainless steel (thickness 1.5 mm) were prepared. The friction stir welding was performed under the 2 wire welding conditions shown in table 4. Friction stir welding was performed until the wire welding length became 10m, and then the presence or absence of breakage of the pin portion or the shoulder portion and the wear amount of the shoulder portion of the tool member were measured. In the test, a backing material composed of a silicon nitride sintered body was used.
The presence or absence of breakage of the pin portion or the shoulder portion was visually confirmed. The wear amount of the shoulder portion of the tool member was obtained for the tool member after the test by using a laser 3-dimensional shape measuring instrument. The results are shown in Table 5 below.
TABLE 4 Table 4
| Conditions (conditions) | Test condition 1 | |
| Rotating speed (rpm) | 500 | 800 |
| Speed of movement (mm/min) | 400 | 800 |
| Press-in load (kN) | 19.6 | 29.4 |
TABLE 5
The results shown in Table 5 above indicate that: the tool members of the various embodiments exhibit excellent performance. In particular, the tool member has a R1/D of 0.05 to 0.15, a R1 of 1.2 to 2.2mm, a R2 of 0.1mm or more, and an inclined surface angle of 3 to 8 DEG, and has a small abrasion loss. In addition, the tool member with the inclined surface having an angle of-3 to-8 degrees is also less in abrasion loss. Therefore, it has been found that the angle of the inclined surface is preferably more than 0 ° and 10 ° or less than 0 ° and-10 ° or more. On the other hand, in comparative examples 1to 3, the tool members were all broken and the welding length of 10m could not be tolerated in the test. These results indicate that: even with the same material, by optimizing the shape, the durability of the tool member is improved.
Examples 1A to 9A
Next, friction stir welding was performed on the tool members of examples 1to 9 by changing the rotational speed and torque. The rotation speed A (rpm) and the torque B (kg.m) were set, and friction stir welding was performed under the conditions shown in Table 6. As a material to be welded, 2 pieces of stainless steel (thickness 1.0 mm) were prepared.
After the welding, the presence or absence of defects in the welded portion was measured. The presence or absence of defects in the welded portion was observed on the cross section of the welded portion by using a metal microscope, and the presence or absence of holes (welding defects) having a diameter of 0.2mm or more was observed. The results are shown in Table 6 below.
TABLE 6
The results shown in Table 6 indicate that: using examples 1, 3 to 5, and 7 to 8 satisfying the preferred ranges, a defect-free welded article can be obtained in the range of B/a=0.001 to 0.025. Further, it was confirmed by a metal microscope (2000 times), and as a result, defects of less than 0.2mm were not seen. Therefore, both durability and welding quality can be achieved.
On the other hand, when the torque is increased, defects occur in the case of deviations from the preferable range as in example 2 (r1=0.4 mm), example 6 (inclination angle 13 °), and example 9 (inclination angle-13 °).
The torque is a quantity expressed by the product of force and distance. Inversely proportional to the distance from the center of the rotation axis. That is, the distal end portion of the tool member is different in the force carried by the rotation shaft and the shoulder portion. The tool member of the embodiment can realize flawless welding by friction stir welding with the B/A in the range of 0.001 to 0.025. In other words, it can be said that the tool member of the embodiment is suitable for friction stir welding under the condition of B/a=0.001 to 0.025.
While the present invention has been described with reference to several embodiments, these embodiments are presented by way of example and are not intended to limit the scope of the invention. These novel embodiments can be implemented in various other forms, and various omissions, substitutions, changes, and the like can be made without departing from the scope of the invention. These embodiments and modifications thereof are included in the scope and gist of the invention, and are included in the scope of the invention described in the claims and equivalents thereof. The above embodiments may be combined with each other.
Symbol description:
1. tool component for friction stir welding
2. Tip end of stirring pin
3. The end of the shoulder part
4. Root of stirring pin part
5. Inclined surface
External diameter of W stirring pin part
D outer diameter of shoulder
Angle of inclination of θ inclined plane
Claims (5)
1. A tool component for friction stir welding, characterized in that: in a tool member for friction stir welding composed of a ceramic member in which a shoulder portion and a pin portion are integrated, a root portion of the pin portion and an end portion of the shoulder portion have a curved surface shape, and a tip portion of the pin portion has a curved surface shape, wherein R1/D is 0.02 to 0.20 when a radius of curvature of the end portion of the shoulder portion is R1 (mm) and an outer diameter of the shoulder portion is D (mm);
the ceramic member is a silicon nitride sintered body in which silicon nitride crystal particles having an aspect ratio of 2 or more per unit area of 50 [ mu ] m by 50 [ mu ] m are 60% or more in terms of area ratio (%);
the silicon nitride sintered body contains 15 mass% or less of an additive component other than silicon nitride, and the additive component contains 3 or more elements selected from the group consisting of Y, lanthanoid, al, mg, si, ti, hf, mo, C;
an inclined surface is provided from the end of the shoulder portion to the root of the stirring pin portion, and the inclined surface has an inclination angle θ of more than 0 ° and less than 10 ° with respect to the direction of the axis right angle of the stirring pin portion;
the radius of curvature R1 (mm) of the end part of the shoulder part is more than 0.5 mm;
the surface roughness Ra of the curved surface shape part formed at the end part of the shoulder part is below 10 mu m;
the ceramic member is composed of a silicon nitride sintered body having a Vickers hardness of 1400HV1 or more.
2. The friction stir welding tool member according to claim 1, wherein: the radius of curvature R2 (mm) of the root of the stirring pin part is more than 0.1 mm.
3. A friction stir welding device, characterized in that: a friction stir welding tool member according to claim 1 or claim 2.
4. A friction stir welding method using the friction stir welding apparatus according to claim 3 characterized in that: 2 or more materials to be welded are stacked together and pushed onto the materials to be welded while rotating the friction stir welding tool member at a rotation speed of 300rpm or more.
5. The friction stir welding method according to claim 4, wherein: the welded material is steel.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
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| JP2016-156384 | 2016-08-09 | ||
| JP2016156384 | 2016-08-09 | ||
| CN201780048238.3A CN109562485B (en) | 2016-08-09 | 2017-08-04 | Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method |
| PCT/JP2017/028458 WO2018030309A1 (en) | 2016-08-09 | 2017-08-04 | Friction stir welding tool member and friction stir welding device using same, and friction stir welding method |
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| CN201780048238.3A Division CN109562485B (en) | 2016-08-09 | 2017-08-04 | Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method |
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| CN201780048238.3A Active CN109562485B (en) | 2016-08-09 | 2017-08-04 | Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method |
| CN202110992426.XA Active CN113681148B (en) | 2016-08-09 | 2017-08-04 | Tool member for friction stir welding, friction stir welding device using same, and friction stir welding method |
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| US (1) | US11130194B2 (en) |
| EP (1) | EP3498415B1 (en) |
| JP (2) | JP7248235B2 (en) |
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| JP6344690B2 (en) * | 2014-08-28 | 2018-06-20 | 三菱重工エンジニアリング株式会社 | Friction stir welding tool and friction stir welding apparatus |
| WO2019235295A1 (en) * | 2018-06-06 | 2019-12-12 | 国立大学法人大阪大学 | Friction stir welding tool and friction stir welding method |
| EP3868507A4 (en) * | 2018-10-15 | 2022-07-27 | Osaka University | Friction stir welding tool member and friction stir welding method using same |
| JP7150570B2 (en) * | 2018-11-13 | 2022-10-11 | 川崎重工業株式会社 | Tool for friction stir welding and friction stir welding method |
| JP2020142293A (en) * | 2019-03-08 | 2020-09-10 | 国立大学法人大阪大学 | Tool for friction stir welding and friction stir welding method |
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| JP3258307B2 (en) * | 2000-01-25 | 2002-02-18 | 川崎重工業株式会社 | Friction stir welding tool with high fatigue strength structure |
| JP4234291B2 (en) * | 2000-01-26 | 2009-03-04 | 川崎重工業株式会社 | Joining tool for friction stir welding |
| JP2003034581A (en) * | 2001-07-24 | 2003-02-07 | Toshiba Corp | Silicon nitride abrasion resistant member and method for producing the same |
| JP3732448B2 (en) | 2002-02-26 | 2006-01-05 | 川崎重工業株式会社 | Spot welding tool |
| JP2007054885A (en) * | 2005-08-26 | 2007-03-08 | Kawasaki Heavy Ind Ltd | Joining tool, and friction stir joining method |
| EP1979121A4 (en) | 2006-01-31 | 2009-10-28 | Sii Megadiamond Inc | Thermally enhanced tool for friction stirring |
| JP2008132524A (en) * | 2006-11-29 | 2008-06-12 | Kurimoto Ltd | Rotary tool for friction stir welding |
| JP5358140B2 (en) * | 2008-08-08 | 2013-12-04 | 株式会社総合車両製作所 | Friction stir welding apparatus and friction stir welding method |
| JP2011098842A (en) | 2009-11-04 | 2011-05-19 | Sumitomo Electric Ind Ltd | Sintered compact and method for manufacturing the same, and rotating tool |
| JP2012139696A (en) * | 2010-12-28 | 2012-07-26 | Sumitomo Electric Ind Ltd | Rotating tool |
| JP2013035009A (en) | 2011-08-05 | 2013-02-21 | Japan Transport Engineering Co | Rotary tool, friction stir welding method using the same, and friction-stir point welding method |
| JP6068804B2 (en) * | 2012-01-26 | 2017-01-25 | 株式会社総合車両製作所 | Friction stir welding method and railcar frame manufacturing method |
| DE102012001877B4 (en) | 2012-02-01 | 2014-01-09 | Christoph Lenz | Kaltnahtstichel for producing a media-tight seam |
| CN104203481B (en) * | 2012-04-06 | 2016-03-02 | 杰富意钢铁株式会社 | The friction stirring connecting method of steel plate |
| JP6251514B2 (en) * | 2013-08-21 | 2017-12-20 | 株式会社フルヤ金属 | Friction stir welding tool |
| JP2015205339A (en) * | 2014-04-23 | 2015-11-19 | スズキ株式会社 | Friction stir welding method and friction stir welded body manufactured by using the same |
| US20170136571A1 (en) | 2014-07-10 | 2017-05-18 | Sumitomo Electric Industries, Ltd. | Rotary tool and joining method |
| JP2016064419A (en) | 2014-09-24 | 2016-04-28 | 日本特殊陶業株式会社 | Tool for friction-agitation connection, and method of manufacturing the same |
| JP6581099B2 (en) | 2014-09-25 | 2019-09-25 | 株式会社東芝 | Friction stir welding tool member made of silicon nitride sintered body and friction stir welding apparatus using the same |
| JP2016078100A (en) * | 2014-10-21 | 2016-05-16 | 株式会社キーレックス | Point-joining tool |
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| EP3498415B1 (en) | 2022-01-12 |
| JP2022091916A (en) | 2022-06-21 |
| CN113681148A (en) | 2021-11-23 |
| US11130194B2 (en) | 2021-09-28 |
| EP3498415A1 (en) | 2019-06-19 |
| EP3498415A4 (en) | 2020-04-01 |
| JPWO2018030309A1 (en) | 2019-06-13 |
| US20190210149A1 (en) | 2019-07-11 |
| JP7248235B2 (en) | 2023-03-29 |
| JP7376050B2 (en) | 2023-11-08 |
| CN109562485A (en) | 2019-04-02 |
| CN109562485B (en) | 2022-04-15 |
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